Molding compositions of high molecular weight and low molecular weight polymers



R. M. PRICE ET AL MOLDING COMPOSITIONS OF HIGH MOLECULAR WEIGHT AND LOW MOLECULAR WEIGHT POLYMERS Dec. 16, 1955 Filed Nov. 28, 1955 QQQQ mibhwml Mtb@ QQ QQQB OQO@

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United MOLDING COMPOSlTIONS OF HIGH MOLECULAR WILIGH'I1 AND LOW MOLECULAR WEIGHl` VPOLYMERS Application November 28, 1955, Serial No. 549,292

6 Claims. (Cl. 260-45.5)

This invention concerns certain new compositionswhich are intimate mixtures of high molecular weight and low molecular weight thermoplastic alkenyl aromatic resins. It relates more particularly to a method of increasing the iiow rate during molding at elevated temperatures and pressures of a normally solid thermoplastic alkenyl aromatic resin of high molecular weight which method comprises forming compositions which are uniform mixtures of certain low -molecular weight alkenyl aromatic resins and high molecular weight alkenyl aromatic resins.

U. S. Patent No. 2,401,266 makes electrical insulating compositions that comprise a mixture of from about 20 to 50 percent by weight of polystyrene having a mean molecular weight of about 80,000 and from 50 to 80 percent of polymerized alpha-methyl styrene having a viscosity of between 100 and 2000 centistokes at 100 F. as plasticizer.

U. S. Patent No. 2,454,851 makes electrical insulating` material which comprises a uniform mixture of from 50 to 70 percent by weight of polystyrene having a molecular weight between 60,000 and 150,000, from 18 to 30 percent of polymerized styrene having a molecular weight of from 6,000 to 30,000 and from l to 20 percent of another plasticizer such as isoamylnaphthalene, phenanthrene, -naphthyl ethyl eth-er, octahydrophenanthrene, etc.

Such plasticized polystyrene compositions are satisfactory for many electrical insulating applications, e. g. for insulation around conductors in cables, where a material is desired which when heated is soft enough to how into the place where it is wanted, and when cooled to ordinary temperatures, it hardens, but the compositions do not .possess properties such as good tensile strength, high heat distortion temperature or resistance to shrinkage upon heating at elevated temperatures, e. g. at temperatures of from 80 to 100 C. which are desired for the manufacture of molded plastic articles.

Polystyrene and other thermoplastic alkenyl aromatic resins are often undesirably resistant to rapid flow during molding at the elevated temperatures and pressures employed in usual compression or injection molding operations or by extrusion methods and dii'liculties have been encountered in producing accurate moldings or extrusions at the rapid rates required in commercial operations. It is known that the rates of flow during mo-lding may readily be increased by incorporating any of a variety of well known plasticizing agents with the resin prior to molding. However, most plasticizers when added in amount suicient for the purp-ose, seriously impair one or more of the properties of the molded product.

For instance, the addition of 10 percent by weight or more of a usual plasticizer or flow agent such as white mineral oil, butyl stearate, dibutyl phthalate, etc., results in a pronounced decrease in the tensile strength and a substantial lowering of the heat distortion temperature of the molded article.

The heat distortion temperature of thermoplastic resins Such as polystyrene or copolymers of styrene and one es atent O ICC is recognized in the art as a measure of the practical heat stability of the resin or of molded articles made 'of the resin against dimensional change upon heating the same at elevated temperatures. Most thermoplastic resins are characterized by a second order transition temperature below which they are rigid, brittle, dimensionally stable and free from cold flow, but above which temperature they are tough, rubbery and subject to flow. The second order transition temperature for polystyrene has hereto fore been indicated to coincide with the heat distortion temperature, see Styrene, lts Polymers, Copolymers and Derivatives, page 509, Reinhold Publishing Corporation, New York, N. Y. (1952). Although the teaching that the second order transition temperature and the heat distortion temperature for polystyrene are the same is correct for polystyrene having an average molecular weight of about 80,000 or greater as determined by the scattering of light, such as molding grade polystyrene, the normally solid thermoplastic alkenyl aromatic resins, e. g. polystyrene, having an average molecular weight lower than 80,000, say from 10,000 to 60,000, have second order transition temperatures which are substantially lower than the heat distortion temperature determined in accordance with the aforementioned test procedures.

It has now been discovered that the normally solid thermoplastic alkenyl aromatic resins of low molecular weight being subject to flow at temperatures above their second order transition temperature and below their heat distortion temperature are eminently suitable for incorporating with thermoplastic alkenyl aromatic resins of high molecular weight for increasing the ilow rate of the high molecular weight resinduring molding at elevated temperatures and pressures without appreciably reducing the heat distortion temperature of the molded article below the heat distortion temperature of the high molecular weight resin alone. Y

Accordingly, it is a primary object of the invention to provide a method of increasing the ow rate during molding at elevated temperatures and pressures of a normally solid thermoplastic alkenyl aromatic resin of high molecular weight without appreciably reducing the heat distortion temperature of the molded article below the heat distortion tempe-rature of the resin alone. Another ob ject is to provide molding compositions comprised essentially of a hard thermoplastic alkenyl aromatic resin of high molecular weight and a minor but effective proportion of a normally solid alkenyl aromatic resin compatible therewith and of relatively low molecular weight to'increase the flow rate during molding at elevated temperatures and pressures without appreciably changing the physical properties such as tensile strength, impactV strength, percent elongation, hardness and heat distortion temperature of the molded article from those of the high molecular weight resin alone. Other and related objects may appear from'the following description of the invert tion. f f

According to the invention, the rate of ow of a normally solid thermoplastic alkenyl aromatic resin of high molecular weight, e. g. polystyrene, having an average molecular weight of at least 140,000, preferably 200,000 or greater, as determined by the scattering of light (see l. Chem. Phys., vol. 18, pp. 830-893, 1950), duringy molding at elevated temperatures and pressures can readily be increased without appreciably reducing theheat' distortion temperature of the molded article below that ot the high molecular weight resin alone, byintimately incorporating with the high molecular weight resin a minor proportion, suitably from 2 to 40 percent by weight, of a normally solid thermoplastic alkenyl aromatic resin of relatively low molecular weight, which resin is compatible therewith, is substantially free from volatile ingredients, has a molecular Weight not more than one-third as great as the molecular weight of the high molecular weight resin and a second order transition temperature at least as high as 45 C. and not more than 5 C. above the second order transition temperature of the high molecular weight resin.

It is important that the high molecular weight and the low molecular weight alkenyl aromatic resin starting materials and the tinal composition or product be free or substantially free from volatile ingredients or additives such as plasticizers, i. e. contain not more than 3, preferably not more than 2, percent by weight of such ingredients.

The thermoplastic alkenyl aromatic resins of high molecular weight toV be employed in preparing the compositions are the normally hard solid polymers and copolymers of one or Amore monovinyl aromatic hydrocarbons of the benzene series such as styrene, vinyltoluene, vinylxylene, ethylvinylbenzene, ethylvinyltoluene, isopropylstyrene, etc.; copolymers of at least 60, preferably from 60 to 85, percent by weight of at least one such monovinyl aromatic hydrocarbon and not mcre than 40, suitably from 40 to 15, percent of a monoalkenyl aromatic hydrocarbon of the benzene series having a single isopropenyl radical directly attached to a carbon atom of the benzene nucleus, e. g. alpha-methyl styrene, alphaethyl styrene or para-methyl-alpha-methyl styrene; and resinous compositions comprising a major proportion by weight of at least one such polymerized aromatic hydrocarbon of high molecular weight and a minor proportion, preferably from 2 to 40 percent by weight, of a rubbery elastomer such as natural rubber or a synthetic rubbery copolymer containing in chemically crmbined firm from 40 to 80 percent by weight of butadiene and from 60 to 20 percent of styrene.

The resinous compositions of high molecular weight containing a minor proportion by Weight of a rubbery elastomer such as natural or a synthetic rubber to be employed as starting material are suitably copolymers of from 85 to 98 percent by weight of one or more mono'- vinyl aromatic hydrocarbons, e. g. styrene or vinyltoluene, andfrom to 2 percent of the rubbery elastomer. Such copolymers can conveniently be prepared by procedure described in United States Patent No. 2,694,692. The high molecular weight resin starting material containing rubber can also be prepared by intimately'incori porating a major proportion by Weight of one or more of the aforementioned high molecular weight alkenyl aromatlc resins with a minor proportion, preferably from 2 to 40 percent by weight, of the rubbery elastomer in usual ways, e. g. by compounding the heat-plastied ingredients with one `another on rolls, la Banbury mixer or a plastics extruder to obtain a uniform composition.

Thermoplastic resinous polymers of high molecular weight of the alkenyl aromatic `hydrocarbons can readily be prepared by polymerizing one or more of the monovinyl aromatic hydrocarbons or mixtures of the monovinyl aromatic hydrocarbonsand a monoalkenyl aromatic hydrocarbon, e. g.. alpha-methyl styrene, in the desired proportions, in usual ways such as by heating the monomers in bulk, i. e. inthe substantial absence of aninert liquid medium. Polymers of monovinyl aromatichydrocarbons can be prepared by procedure described in `United States PatentNo. 2,530,409. Copolyrners'of the monovinyl aromatic hydrocarbons and a monoalkenyl aromatic hydrocarbon, e.` gf copolymers of styrene and alpha-i methyl styrene, can be prepared by procedure described 1n United States Patent` No. 2,638,465. The alkenyl aromatic resins-of high molecular weight are usually devolanhzedrby rheating the resin. to its melting temperature or above under reduced pressure to vaporize and remove volatile ingredients, so as to obtain a polymeric material which is free or substantially free, i. e. contains not more than 3, preferably not more than 2, percent by weight of volatile ingredients such as dimers, trimers, or tetramers which volatile ingredients tend to lower the heat distortion temperature of the polymer.

The alkenyl aromatic resins of low molecular weight to be employed as starting materials for increasing the ow rate of the normally solid high molecular weight alkenyl aromatic resins during molding at elevated temperatures and pressures are the homopolymers and copolymers of one or more monoalkenyl aromatic hydrocarbons of the benzene series having a single polymerizable group of the formula CH2=CR wherein R represents a member of the group consisting of hydrogen, the methyl and ethyl radicals, directly attached to a carbon atom of the benzene nucleus. Examples of suitable monoalkenyl aromatic hydrocarbons are styrene, vinyltoluene, vinylxylene, ethylvinylbenzene, isopropylstyrene, ethylvinyltoluene, alpha-methyl styrene, alpha-ethyl styrene or para-methyl-alpha-methyl styrene.

The low molecular weight polymers of the alkenyl aromatic hydrocarbons can be prepared in usual ways such as by polymerizing the monomers in an inert liquid organic solvent and in the presence or absence of a catalyst, or by heating the monomers in bulk at elevated temperatures and pressures. The molecular weight of the low molecular weight polymers can be controlled by varying the proportion of solvent employed or the temperature at which the polymerization is carried out. Usually, an increase in the proportion of solvent employed results in the formation of a polymer of lower molecular Weight, under otherwise similar polymerization conditions, and an increase in the polymerization temperature results in the formation of a polymer of lower molecular weight. More specifically, the low molecular Weight polymers of monovinyl aromatic hydrocarbons, e. g. styrene or vinyltoluene, can readily be prepared by heating the monomers in bulk at temperatures between about 130 and 320 C. under pressure. The low molecular weight homopolymers of, and copolymers of two or more, monoalkenyl aromatic hydrocarbons such as alpha-methyl styrene, alpha-ethyl styrene or para-methyl-alpha-methyl styrene can conveniently be prepared by polymerizing the monomers in an inert organic solvent such as chlorobenzene, ethylbenzene, toluene or isopropylbenzene in the presence of a bleaching earth or clay as catalyst at temperatures between 70 C. and about 90 C. or above. Copolymers of low molecular weight can be prepared from mixtures of the monovinyl aromatic hydrocarbons and monoalkenyl aromatic hydrocarbons by the procedures just mentioned. The low molecular weight copolymers containing a major proportion by weight of a monovinyl aromatic hydrocarbon, e. g. styrene, and a minor proportion of an alkenyl aromatic hydrocarbon such as alpha-methyl styrene are usually prepared by heating a mixture of the monomers in bulk at elevated temperatures between 130 and 320 C. The low molecular' Weight copolymers of a major proportion by weight of an alkenyl aromatic hydrocarbon, e. g. alpha-methyl styrene, and a minor proportion of a monovinyl aromatic hydrocarbon such as styrene can be prepared by polymerizing such a mixture of the monomers in an inert solvent in the presence of a catalyst at temperatures of from -70 to about C.

It is important that the low molecular weight alkenyl aromatic resin be free or substantially free from volatile ingredients, i. e. contain not more than 3, preferably not more than 2 percent by weight ofvolatile ingredients, have a second order transition temperature at least as high as 45 C., which second order transition temperature may Vbe as high or up to 5 C. higher than the second order ,transition temperature of the high molecular weight allzenyl aromatic resin with which it is incorporated, and

a molecular weight not greater than one-third as great as the average 'molecular weight of the high molecular weight alkenyl aromatic resin. For example, when employing polystyrene having an average molecular weight of about 180,000 as the high molecular weight resin starting material, suitable low molecular weight alkenyl aromatic resins to be incorporated therewith for increasing the ow rate during molding at elevated temperatures and pressures of the high molecular weight alkenyl aromatic resin are the low molecular weight resins of polymerized aromatic hydrocarbons such as styrene, vinyltoluene, alpha-methyl styrene or copolymers of styrene and alpha-methyl styrene, which polymers are substantially free from volatile ingredients, i. e. contain not more than 3, preferably not more than 2, percent by weight of volatile ingredients capable of being vaporized and removed by heating the polymer at a temperature of 213 C. at one millimeter absolute pressure for a period of 25 minutes, and which low molecular weight polymers have average molecular Weights between about 60,000 and a lower value corresponding to a second order transition temperature for the polymer at least as high as 45 C.

The proportions of the high molecular weight resin and the low molecular weight resin relative to one another can be varied widely, depending for the most part upon the difference between the average molecular weight of the low molecular resin and the average molecular weight of the high molecular weight resin with which it is intimately incorporated. In general, the low molecular weight polymers of monovinyl aromatic hydrocarbons such as polystyrene or polyvinyltoluene having average molecular weights between about 10,000 and 40,000 and second order transition temperatures between about 45 and 65 C. can be employed in amounts of from 2 to 20, preferably from 5 to 15, percent by weight of the sum of the weights of the low molecular Weight resin and the high molecular weight resin used. The low molecular weight polymers such as polystyrene or polyvinyltoluene having average molecular Weights of 45,000 or above, e. g. from 45,000 to 90,000, can be employed in amounts of from 2 to 40, preferably from 5 to l5, percent by weight of the final composition. The low molecular weight polymers of monovinyl aromatic hydrocarbons are preferably polymers having molecular weights of from 10,000 to 60,000. The low molecular weight resins of polymerized alkenyl aromatic hydrocarbons such as alpha-methyl styrene, alpha-ethyl styrene or para-methyl-alpha-methyl styrene, which resins have average molecular weights of at least 1000, preferably from 1000 to 6000, and second order transition temperatures at least as high as 45 C. and not more than 5 C. higher than the second order transition temperature of the high molecular weight resin with which it is incorporated, are usually employed in amounts of from 2 to 20, preferably from 5 to 15, percent by weight of the composition.

The effect of the low molecular weight resin for increasing the flow rate of the high molecular weightl resin during molding atk elevated temperatures and pressures becomes greater as the difference between the average molecular weight of the low molecular weight resin and the average molecular weight of the high molecular weight resin, with which it is incorporated, increases. More specifically, a small amount, e. g. l0 percent by weight, of polystyrene having an average molecular weight of about 20,000 when intimately incorporated with 90 percent by weight of polystyrene having an average molecular Weight of 275,000 has an effect of increasing the flow rate of the high molecular weight polystyrene which is substantially equivalent to the increase in ow rate obtained by incorporating 40 percent by weight of polystyrene having an average molecular weight of about 80,000 with percent by weight of the polystyrene of molecular weight of 275,000. l

The compositions comprising thexhigh molecular weight and the low molecular weight alkenyl aromatic resins intimately and uniformly incorporated with one another'lv and which compositions have improved flow rates duringy molding at elevated temperatures and pressures over flow, rates of the high molecular weight resins, alone, under otherwise similar molding conditions, can be prepared by intimately incorporating from 2 to 40, preferably from 5 to 15, percent by weight o f the low molecular weight alkenyl aromatic resinV with from 98 to 60, preferably from to 85, percent of the high molecular Weight resin.

The resins can be intimately incorporated with one another in any usual Way. The resins can be heat-plastied and mechanically worked with one another on compounding rolls, a Banbury mixer or in aplastics extruder and at temperatures between about and 280 C., preferably in the absence or substantial absence of air or oxygen. The resins can be dissolved or dispersed in an organic liquid such as benzene, toluene, xylene, ethylbenzene, ethyltoluene, etc., to form a solution or intimate dispersion containing the high molecular weight and the low molecular weight resins in the desired proportions, after which the solvent is removed in usual ways, e. g. by evaporation of the solvent at elevated temperatures and under reduced pressures. The compositions can be prepared by dissolving the low molecular weight polymer in monomer, e. g. dissolving low molecular weight polystyrene or polyvinyltoluene in monomeric styrene, in the desired proportions, then heating the solution to polymerize the monomer under conditions which form high molecular weight polymer such as by heating the solution in bulk or dispersed in an aqueous medium such as water or brine at temperatures between about 80 and 210 C. and at atmospheric or superatmospheric pressures.

The high molecular weight polymer and the low molecular weight polymer can conveniently be incorporated with one another by mixing or blending granules of the solid polymers in the desired proportions and feeding the mixture into a plastics extruder wherein it is heatplastied and mechanically worked at temperatures between about 140" and 280 C. until a uniform composition is obtained, then is extruded, preferably devolatilized, and cooled and out or ground to a granular form suitable for molding. In all such blending operations it is essential that the heat-plastified polymers be maintained or mechanically worked with one another under time and temperature conditions which do not result in any appre- .ciable deterioration o-f the polymers, e. g. to form volatile ingredients such as monomers, dimers, trimers or tettramers, or polymers of lower molecular weight than either of the polymer starting materials, because such formation of by-product ingredients tends to result in lowering of the heat distortion temperature of the composition.

The efficiency of the effect of the low molecular weight polymer for increasing the ow rate of the high molecular weight polymer during molding at elevated temperatures and pressures, appears to be greatest when the high molecular weight polymer is caused to flow by application of an applied molding pressure, under conditions of high shearing stress.

The effect of the low molecular weight polymers for increasing the flow rate of the high molecular lweight polymer during molding at elevated temperaturesand pressures can readily be determined by observing the temperature at which the ow rate of the high molecular weight polymer alone is just suicient to ll a given mold under application of 'a predetermined molding pressure in a stated period of time, and observing the temperature at which the owrate of a composition consisting of an intimate homogeneous mixture of the high molecular weight polymer and a low molecular weight polymer is just sufcient to till the mold under the same applied molding pressure and time. By such procedure one obtains a measure of the effect which results in an increase in ow rate of the high molecular weight polymer due to the low molecular weight polymer incorporated therewith, expressed in terms of lowered molding temperature. The

7 temperature at which the ow rate of the material is just suicient to completely lill a mold under given molding pressure and time conditions is herein referred to as the flow temperature.

The flow temperature constitutes an indirect, but readily determined, measure of the tlow rate during molding at elevated temperatures and pressures of a normally solid thermoplastic alkenyl aromatic resin. The difference' between the flow temperature of a high molecular weight thermoplastic alkenyl aromatic resin alone, and the ow temperature of an intimate mixture of the high molecular weight resin and an alkenyl aromatic resin of low molecular weight, under similar conditions of molding pressure and time is a measure of the effect of the low molecular weight resin for increasing the ow rate of the high molecularV weight resin during molding. The dow temperature becomes lower as the applied load or molding pressure is increased. At constant load, the flow temperature becomes lower with increase in eiciency of the effect of the low molecular weight resin, and becomes lower with increase in the proportion of the low molecular weight resin employed.

By varying the molding pressure applied to a given polymeric material and observing the tlow temperature for different molding pressures one obtains a series of temperature values which can be plotted on coordinates of temperature versus applied molding pressure and a smooth curve drawn through the points to obtain a tlow diagram for the polymer.

Figs. 1-2 of the drawing illustrate such flow diagrams and are more particularly hereinafter described with reference to the examples.

It may be mentioned that the effect of increasing the tlow rate during molding at elevated temperatures and pressures of a high molecular weight thermoplastic resin due to intimately incorporating a small proportion of a low molecular weight alkenyl aromatic resin therewith, is more pronounced and results in greater improvement in the compositions when both the high molecular weight resin and the low molecular weight resin are composed of polymer molecules of relatively narrow molecular weight distribution. Best results are usually obtained when each of the polymeric starting materials has a narrow range of molecular weights and contains not more than two percent by weight of volatile ingredients, e. g. monomers, dimers, trimers or tetramers, and the polymeric starting materials are intimately incorporated with one another to form a homogeneous composition, suitably by heat-plastifying and mechanically working the ingredients with one another, under conditions which do not result in any appreciable deterioration of the polymers so as to obtain a final product containing volatile ingredients in amount not substantially lgreater than that of the starting materialsv This invention provides a method of readily increasing the flow rate during molding at elevated temperatures and pressures, e. g. at molding pressures of from 5,000 to 20,000 pounds per square inch gauge pressure, of a normally solid thermoplastic alkenyl aromatic resin without appreciably reducing the heat distortion'temperature of the molded article below that of the high molecular weight resin alone. The invention provides a method for making molding compositions free or substantially free `from liquid 0r volatile plasticizers and possessing good mechanical properties, which compositions are useful for a variety of applications in the home and industry.

The compositions comprising essentially a thermoplastic alkenyl aromatic resin of high molecular weight having uniformly incorporated therewith a normally` solid alkenyl aromatic resin of relatively low molecular weight as the sole ow agent for increasing the ow rate during molding at elevated temperatures and pressures of the high molecular weight resin possess good mechanical properties such as tensile strength, impact strength, percent elongation, hardness and high heat distortion S temperature which render the compositions suitable for use in the manufacture of molded articles which are useful in a variety of applications.

Small -amounts of additives such as dyes, pigments, coloring agents, antioxidants, stabilizers, lubricants, mold release agents or plasticizers, if desired, can be incorporated with the compositions. Such agents when used in the compositions are usually employed in amounts corresponding to from 0.1 to 2 percent by Weight of the final product, but such additives are not required in the invention.

The following examples illustrate Ways in which the principle of the invention has been applied, but are not to be construed as limiting its scope.

EXAMPLE 1 In each of a series of experiments, a composition was prepared by intimately incorporating polystyrene of low molecular weight and polystyrene of high molecular weight with one another in proportions as stated in the following table. The low molecular weight polystyrene employed in the experiments contained 0.71 percent by weight of volatile ingredients and 3.5 percent of methanol soluble substances, had a viscosity characteristic of 6.1 centipoises (l0 weight percent solution of the polystyrene in toluene at 25 C.), an average molecular weight of 82,000 (light scattering) and a second order transition temperature of 81.5 C. The procedure for determining the volatile ingredients was to heat a weighed portion of the polymer at a temperature of 213 C. at 1 millimeter absolute pressure for a period of 25 minutes, then cool and reweigh. The loss in weight represents volatile ingredients. The procedure for determining methanol soluble substances was to dissolve a weighedA amount of the polymer in dioxane, precipitate the polymer in methyl alcohol, separate, wash and dry the precipitate and determine its weight. The loss in weight represents methanol soluble substances. It is to be noted that the percent methanol soluble substances determined by the test includes the percent of volatile ingredients. The average molecular weight of the polystyrene was obtained by determining the intrinsic viscosity for the polystyrene in toluene and reading the molecular weight from a graph plotted on coordinates of intrinsic viscosity versus molecular weight by light scattering (see Outer, Carr and Zimm, J. Chem. Phys., vol. 18, pp. 830-839, No. 6, June 1950). The procedure for determining the second order transition temperature was similar to that described in ASTM D864- 45T. The high molecular weight polystyrene employed in the experiments contained 0.15 percent by weight of volatile ingredients, and contained 0.84 percent of methanol soluble substances, had a viscosity characteristic of 31.1 centipoises, an average molecular weight of 290,000, a second order transition temperature of 83 C. anda heat distortion temperature of 86 C. Both the high molecular weight polystyrene and the low molecular weight polystyrene employed in the experiments were composed of polymer molecules of narrow molecular weight distribution. In preparing the compositions the low and the high molecular weight polystyrenes were mixed in granular form in the desired proportions. The mixture was fed to a Vplastics extruder wherein it was heat-plastied at temperatures between 365 and 395 F., mechanically worked and extruded through a die, then cooled and cut to a granular form. Each mixture was passed through the plastics extruder two times. The product was injection molded to form test pieces 6.5 inches long having the end portions of ls x 3%: inch cross section by l/s inches long tapering to a mid-portion of 1A: x 1/2 inch cross section by 3 inches long. The test pieces were molded on a standard plastics injection molding machine having 'a tunnel capacity such that the polymer was heated therein for a period of time of about 200 seconds when the machine wasoperated on a 45 second molding cycle to form a test bar. The procedure for injection molding a test bar was to maintain the molding pressure applied to the plastic at a constant value, e. g. 5000 pounds per square inch, and

polymer during molding at elevated temperatures and pressures. The difference between the flow temperature of the high molecular weight alkenyl aromatic resin alone, and the ow temperature of a composition of the high change the temperature at which the polymer was heated molecular weight resin and the low molecular weight until the ow rate of the plastic under the applied moldresin under similar molding pressures is a measure of ing pressure was just suicient to ll the mold in a pethe effect of the low molecular weight resin for increasriod of 45 seconds. The flow temperature, i. e. the teming the flow rate of the high molecular weight resin durperature at which the ilow rate of the polymer was just ing molding. By plotting the iiow temperature values suicient to completely ll the mold under the applied Versus molding pressure values given in the above Table load in a period of 45 seconds, was observed, The I and drawing a smooth curve through the points, one flow temperature was determined for molding test pieces obtains a ow diagram for the resin. Fia.` 1 ofthe drawof the composition at pressures of 5000, 7000, 9000, ing shows the ow diagrams obtained for the resins given 11,000 and 13,000 pounds per square inch, Test pieces in Table I above. The llow temperature is lowered with of the composition injection molded at 13,000 pounds increase n the proportion of the low molecular weight per square inch were immersed in water at a' tempera- IeSin emPlOYed Without aPPl'eCiahlY Tedueing the heat ture of 97 C, for a period of 30 minutes, then removed, distortion temperature of the composition below that of allowed to cool to room temperature and measured to the high molecular Weight Pell/styrene alone. determined the amount of linear shrinkage upon heating at the elevated temperature. Other test pieces were EXAMPLE 2 injection molded under an applied molding pressure of A Charge 0f 1250 grams 0f granular Poli/styrene 0f 10,000 pounds per square inch and at a temperature A high molecular Weight similar to that employed in EX- of F. above the ow temperature. These test pieces ample l, WaS miXed With 140 grams Of granular 10W were used to determine the tensile strength and percent molecular Weight polystyrene The 10W molecular Weight elongation values for the composition employing pro- 25 polystyrene employed in the experiment contained 1.7 cedures similar to those described in ASTM Doss-49T. percent by Weight of volatile ingredients and 30 percent The impact Strength was determined by procedure sin-1i of methanol soluble substances, had a viscosity characlar to ASTM D256-47T. The heat distortion temperateristie 0f 1.7 eentipeises, an average molecular Weight ture was determined by procedure Similar to that de. of about 19,000 and a second order transition temperascribed by Heirholzer and Boyer, see ASTM Bull. No. 3o' tufo 0f 4 6 C Themixture ofthe granular POlYS'tYI'eneS 134 of May 1945, employing test bai-S of 1/5 X 1/2 ineh was fed into a plastics extruder wherein it was heated at cross section by 2% inches long. temperatures between 330 and 3 40" F., thoroughly For purpose of Showing the increase in 110W rate of blended and extruded through a die, then cooled and the high molecular weight polystyrene during molding Crushed t0 a granular f 0Hn- The PlOduCt Vf/aS lnleetlOn due to incorporating the 10W molecular polymolded t0 form pleCeS-alld t() detelmlne the HOW styrene therewith, and to minimize any effect which may 'temperaturen at Various melding Pleasures .emPlOi/lng PTO- have been caused by mechanical working of the heat- CedufeS Sltnllar t0 thOSe emPlOyed 1n EXample l- The plastified polymer in the extruder, a portion of the batch Product had the PIOPeltleS vof the highmolecular weight polystyrene was fed to the Tensile Strength ibs./sq in 5640 plastics extruder and mechanically worked therein at lo Eiongation "percent" 2 0 temperatures between 390 and 395 F., then extruded, Notched impact Strength w'nnitfibs 0.54 cooled and cut to a granular form. This material was Heat distortion temperature o C 83 injection molded to form test bars and to determine the ow temperature as described above. Table Iidenties the The flow temperature for the ProduCt oder an aPPllod compositions by giving the proportions of the high molecload as Stated below Was as follows: ulai weight and the low molecular weight polystyrene Molding pressure Temperature, employed in preparing the same. The table gives the ibs/SCL im o R tensile strength values and the heat distortion tempera- 5 000 515 ture for the composition. The table also gives the per- 7000 470 cent of linear shrinkage of a test bar of the composition 9000 445 and also gives the now temperature, i. e. the tempera- 11000 420 ture at which the flow rate of the polymeric composition 13000 405. was just suilcient to ll the mold in a period of 45 sec- Y onds under an applied molding pressure as stated in the Fig. 2 of the drawing shows a flow diagram for the comtable. 55 position. For purpose of comparison, a ow diagram Table I Starting Materials Product Molding Pressure Run No. High mol. Low mol. Notched Heat Dis- Shrinkage wt. Poly- Wt. Poly- Tensile Elonga- Impact tortion in30n1in. 5,000 7,000 9,000 11,000 13,0

styrene, styrene, Strength, tion, Strength, Temp., at97 C., p. s. i. p. s. i. p. s. i. p. s.i. p.s 1 percent percent 1bs./sq.1n. percent ft.lbs. C. percent Temp., Temp., Temp, Temp., Temp., F. F. F. F. F.

100 o e, 850 3. 5 o. 44 se 555 505 470 445 430 9o 10 e, 880 3. 0 o. 47 se 3. 94 535 490 465 44o 425 so 20 6, 54o 2. e 0. 45 a5 4. 47 520 480 45o 435 42o 30 5, 000 2. 2 0.42 85 4. 26 51o 475 450 43o 415 6o 4o s, 70o 2. o o. 4s se 4. 47 495 455 445 425 41o The tlowl temperature constitutes an indirect, but

for the high molecular weight polystyrene alone, is inreadily determined, measure of the flow rate of the cluded in Fig. 2 of the drawing. Thus, the difference EXAMPLE 3 Polystyrene of low molecular weight and similar to that described in Example 2, was dissolved in monomeric following table. The mixture-of the granular polymers was'ifed` into a plastics extruder wherein it` washeated and blended into a uniform composition at temperatures between 330 and 340 F., thenextruded through a die, cooled and cutto a granular form suitable-for molding. The composition was-'injection molded Aand tested as described in Example 1. Table Il identifies the compositions `by giving the proportions of the high molecular weight copolymer and the low `molecular weight polystyrenes employed in preparing the same, and the propertics of the low molecular weight polystyrene. The table also gives the properties for the composition.

Table II Starting Materials Product Low rnol. wt. Polystyrene Molding Pressure High mol. Run Wt. Copoly- Notched Heat Dis- No. nier of Second Tensile Elonga- Impact tortion 5,000 7,000 9,000 11,000 13,000 styrene and Vola- MeOH Order Strength, tion, Strength, Temp., p. s. i. p. s. l. p. s. l. p. s. l p. s. l. 5% rubber, Pertile, Soluble, transition mol. lbs/sq. in. percent tt.lbs. C.

percent cent percent percent Temp., wt.

C. Temp., Temp., Temp., Temp., Temp.,

F. F. .F. F. F.

0 4, 170 19. 8 i 2. 2 74 515 ,i 450 420 395 385 80 20 1A 7 30 46 19, 000 4, 660 10. 0 1. 5 73 430 385 365 350 345 80 20 3. 0 21.4 48 28, 000 4, 510 11.3 -1. 6 74 `440` 395 375 360 350 80 20 1.8 11. 8 64 40, 000 4, 500 12. 7 V1. 4 74 455 '410 385 370 360 styrene to form a solution containing two percent by EXAMPLE 5 weight of the low molecular weight polystyrene. The solution was placed in a pressure resistant vessel and agitated and heated at temperatures between and C. under 80 pounds per square inch gauge pressure until a test portion of the solution withdrawn from the vessel showed it to contain 18.3 percent by weight of polymer. Thereafter, the material was removed from the vessel. The polymer was recovered by distilling oil? the monomeric styrene and heating the polymer-at temperatures between 200 and 210 C. at an absolute `pressure of 10 millimeters. The product contained 0.77 percent by weight of volatile ingredients, had a viscosity characteristic of 14.3 centipoises and an average molecular weight of 170,000. The product contained 1l percent by weight of the low molecular weight polystyrene starting material. The product was injection molded and tested employing procedures similar to those employed in Example l; The product had the properties:

Tensile strength lbs./sq.'in 5440 Elongatiou percent 2 Notched impact strength a -ft.lbs 0.45 Heat distortion temperature C-- 86 The ow temperature for the product under an applied molding pressure as stated below was as follows'.

EXAMPLE 4 ln each of a series of experiments, a charge of 1120- gr ms of batch of a granular copolymer of 95 percent by weight of styrene and 5 `percent of a synthetic GR-S bber containing in chemically combined form about r 75 ercent by weight of butadiene and 25 percent of st rene, which copolymer of styrene and rubber was of high molecular weight and had a heat `distortion temperature of 74 C., was mixed with A280 gramsof granular` polystyrene of low molecular weight as identified in the In each of a series of experiments a composition was prepared by intimately incorporating low molecular weight polystyrene with high `molecular weight polystyrene similar to that described in Example l and in proportions as stated Ain the following table. The'low molecular weight polystyrene employed in the'experiments was prepared by polymerizing monomeric styrene by heating the same in #bulk under pressure lin acontinuous polymerizer for polymerization time and temperature conditions of `190 C. for 5 minutes; 300`-3201`,C. for l5 minutes; and 240 C. for 40 minutes,then discharging, cooling and crushing the product to a granular form. The product consisted of about 96 percent lby weight of polymer and about 4 percent of volatile ingredients. AThe polymer was purified vby-dissolving the product inmcthyl ethyl ketone to form a-solution containing `approximately 20 percent by weight of the polymer, pouring the solution into about ve times its volume ofhvigorously agitated methyl alcohol to precipitate the polymer and separating, washing,` dryingand grinding `the` precipitated polystyrene to a granular form.` ,The purified `low inolecular Weight polystyrene employed in Hthe `expe'riments contained 0.77 percent by weight of volatile ingredients and 14.28 percent of methanol soluble substances, had a viscosity characteristic of 2.3 centipoises (l0 weight percent solution of the polystyrene in toluene at 25 C.), an average molecular weight of 27,000 (light scattering)l a second order transition temperature of 64.5 C. and a heat distortion `temperature of 72 C. In preparing the compositions, the low molecular iweight polystyrene and the high molecular weight polystyrene powdered or granular form were mixed together .in 4the desired proportions. The mixture was fed to a'laboratory plastics extruder wherein it was heat-plastied at temperatures between 375 and 4l0 F. and mechanically worked, then extruded through a die, cooled and cut to a granular `form. Each mixture was passed through the plastics extruder two times. The composition wasinjection `molded to form test bars and to determine its -molding characteristics employing procedures similar tothosc employed in Example l. Table Ill identies the com positions and gives-:the proportions-in-percentby weight of` the high molecular iweightland Vthe, lou/molecular weight polystyrenes employed in preparing the same.

, 13 The table also gives the properties determined for the product or composition.

14 weight copolymer of 6,5 percent by weight of styrene and 35 percent of alpha-methyl styrene. The copolymer of Table III Starting Materials Product Molding Pressure Run No. High mol. Low mol. Notched Heat Dis- Wt. Polywt. Poly- Tensile Elonga- Impact tortion 5,000 7,000 9,000 11,000 13,000 styrene, styrene, Strength, tion, Strength, Temp., p. s. i. p. s. i. p. s. i. p. s. i. p. s. i. percent percent lbs/sq. iu. percent .-lbs. C.

T T T T u T -i 31%? 3%? 3%? 5%? 5%? 132 2 ea te as at as a et et 90 10 61995 2f 7 o 46 ss 525 480 450 430 415 80 20 5, 840 2. 0 0. 45 s6 505 465 44o 420 405 EXAMPLE 6 styrene and alpha-methyl styrene of low molecular weight A charge of 1350 grams of a batch of granular molding was prepared by heating a mixture of 65 percent by weight grade polystyrene containing one percent by weight of of monomeric siyrene and 35 perceni of iiioiicfmeric aipha white mineral oil as lubricant and 150 grams of granular methyi styrene in a dosed Vessei. with agitation at a tem polyvinyltoluene of low molecular weight were mixed. Parature of 170 C' until .approximatiy 50 Percent of the The mixture was heat-plastied and blended into a unin ioiiomeis were poiymeiized and Witiidiliwing ih e soiu' form Composition in a plastics extruder employing pro tion.l The polymer was recovered by rapidly heating the cedure similar to that employed in Example 5. The comsoiiition to a temperature of 25.0. .C' under prfissuie and position was injection molded and tested employing pr0 feeding the same into a devolatilizing zone maintained at cedures Simar to those employed in Example 1 The absolute pressures of from 25 to 30 millimeters wherein low molecular weight polyvinyltoluene employed in the iiie miiomeiwere Vapiizd aiifi Separateiy Withiraw' experiment contained 2.83 percent by weight of volatile ing iii".vapoiized goiatilie ingredientsfland ghe pohygier ingredients and 15.35 percent of methanol soluble subfrom Sad 2me' TTlPO ymi was ego ed an cis hio stances, had a Viscosity characteristic of 3.1 centipoises a graiiu ar omi e Clipo ymer o. styrene an. ap a` (10 weight percent solution of the polyvinyltoluene in meiiiyi styrene. empioyed iii ih? expeiimeiit contained 0'54 toluene at 25 C) an average molecular weicht of ap percent byweight ofgvolatile ingredients and' 1.58 percent proximately 39 O00 and a second order transtion tem 35 of methanol soluble substances, had a viscosity characterperature 0f 47a C The molding grade polystyrene em istic of 4.6 centipoises (10 weight percent solution of the ployed in the experiment contained 1.5 percent by Weight coiiorilymer iii toiiiene t Orai averge. moieciiar of volatile ingredients and 3.8 percent of methanol soluble Weig t ofdapproiiiiiigte y ig ft iii-ital an a substances, had a viscosity characteristic of 31 centipoises Second or er transition iempi'rati'irep l e mixat 25 C., an average molecular weight of 285,000, a sec- .40 iure of the graiiuiar poiymeric starting maiteriais was fed 0nd Order transition temperature of 72 C' and a heat into la laboratory plastics extruder wherein 1t was c,heatdistortion temperature of 82 C. For purpose of compari- Piastied and bieiided at temperature? between 375 and son, a portion of the batch of the molding grade poly 410 F. for a period of about 11/2 minutes, then was exstyrene alone was injection molded and tested employing truded iiirfmgh a .die 'coofiei aiiil'crulshefi to a gauuia procedures similar to those employed for the composition fbclm drrhis mateiaiwas eA to fe p astics eXti-ii er an of the polystyrene and the low molecular weight polybeied a ,lscon gime' .lim Pim coliiilositign Wag vinyltoluene. The properties for the polystyrene are reo tame. e Pro uci. las inieciion m0 e ail teste ported below under the heading A, and for the composiemploying pmceduie? Similar @those employed in Exam' tion of the polystyrene and the low molecular weight poly- Pie i' The Composition had the properties: vinyltoluene under the heading B. The properties were: Tensile strength lbs./sq. in 7360 Elongation percent 3.4 A B Notched impact strength ft..1bs 0.42 Heat distortion temperature C 9 3 %ifiye%itrti:1:22:22: "":ifif 103 i8 55 The ow temperature for the product under a molding Tensile strength 1bsI3/esr%1i11% 6, 285 6, 02 Y pressure as stated below was as follows:

- @l 03g Molding pressure, Temperature,

lbs/sq. in. F.

The flow temperature for the polymeric materials under a molding pressure as stated below was: 9000 470 t A B 11,000 495 Molding Pressure, 1bs./sq. in. 137000 430 Temperature, F. 65 EXAMPLE 8 A charge of 1170 grams of granular molding grade giggg- 25 gg polystyrene similar to that employed in Example 6, and 9:0002- 425 4 20 130 grams of solid particles of polymerized alpha-methyl gggg styrene of low molecular weight were mixed. The mix- 70 ture was fed to a laboratory plastics extruder wherein it was heat-plastiiied at temperatures between 375 and 405 EXAMPLE 7 F., mechanically worked during passage therethrough for A charge of 1260 grams of granular high molecular a period of about 11/2 minutes, then was extruded through weight polystyrene similar to that employed in Example 1, a die, cooled and cut to a granular form. The mixture was mixedfwith igrams of a granular low molecular 75 was passed twice through theextruder.Y Thereafter it was injection molded and tested employing lprocedures similar to those employed in Example 1. The low molecular weight homopolymer of alpha-methyl styrene employed in the experiment contained 0.60 percent by weight of volatile ingredients and 1l percent by weight of methanol soluble substances, had an average molecular weight of 1800 and a second order transition temperature of 74 C. The composition had the properties:

Tensile strength lbs./sq. in 5840 Elongation percent 2.2 Notched impact strength ft.lbs 0.38 Heat distortion temperature C 83 The ow temperature for the composition under a molding pressure of 5000 pounds per square inch was 485 F.

EXAMPLE 9 A charge of 1350 grams of granular polystyrene of high molecular weight and similar to that employed in Example l, and 150 grams of solid particles of polymerized alpha-methyl styrene of low molecular weight were mixed. The mixture was fed to a plastics extruder and blended into a uniform composition employing procedure as described in Example 8. The product was injection molded and tested employing proceduresv similar to those employed in Example 1. The low molecular weight horno polymer of alpha-methyl styrene employed in the experiment, contained 2.68 percent by weight of volatile ingredients and 34.6 percent of methanol soluble substances, had an average molecular weight of 1150 and a second order transition temperature of 58 C. The product had the properties:

Tensile strength ..1bs./sq. in-- 7010 Elongation percent 2.8 `Notched impact strength ft.lbs 0.49 Heat distortion temperature C 85 The flow temperature for the product under a molding pressure as stated below was:

Molding pressure, Temperature,

lbs./sq. in. "F

EXAMPLE 10 three minutes, then was removed and allowed to cool and cut to a granular form suitable "for molding. The cornposition was injection molded and `tested employing procedures' similarto those employed in Example 1. The low `molecular weight polystyrene employed in the experimentwas prepared'and purified by Vprocedures similar to those described in Example 5. The low molecular weight polystyrene contained 0.75 rpercent by weight of vlatileingredients and 14.28 percent of methanol soluble substances,had a viscosity characteristic of 2.45 centipoises .'(10 weight percent of the polystyrene in toluene Y molecular weight polystyrene under the heading B. The

at 25 CJ. an average molecular weight of 29,000 and a second order transition temperature of 64 C. For purpose of comparison a composition of 780 grams of the polystyrene of high molecular weight and 420 grams of .the rubbery copolymer of butadiene and styrene was prepared .by compounding the Vpolymeric ingredients with one another in the Banbury fnixer for similar time and` properties for the compositions were:

Tensile Strength .-lbs./sq. in.- 4, 340 4, 255 Elongation 26. 3 17. 3 N otehed Impact Strength 9. 4 5. 7 Heat Distortion Temperature C.. B2 79 The ow temperatures for the compositions under a molding pressure as stated below were:

A B Molding Pressure, 1bs./sq. in.

Temperature, F.

trono- 420 395 13,000-. 405 aso We claim:

1. A resinous composition consisting of from 60 to 98 percent by weight of a normally solid thermoplastic alkenyl aromatic resin A selected from the group consisting of (l) a polymerized monovinyl aromatic hydrocarbon of the benzene series, (2) copolymers of at least 60 percent by weight of a monovinyl aromatic hydrocarbon of the benzene series and not more than 40 percent of an alkenyl aromatic hydrocarbon of the benzene series having a single isopropenyl radical directly attached to a carbon atom of the aromatic nucleus and (3) resinous products consisting of from 60 to 98 percent by weight of at least one of the polymers of 1 and 2 and from 40 to 2 percent of a rubbery elastomer which is a member of the group consisting of natural rubber and rubbery copolymers of from 40 `to 80 percent by weight of butadiene and from 60 to 20 percent of styrene, the said resin A containing not more than 3 percent by weight of volatile ingredients capable of being vaporized and removed by heating the resin at a temperature of 213 C. at one millimeter absolute pressure for a time of 25 minutes and having an average molecular weight of at least 140,000, as determined by the scattering of light, intimately incorporated with 40 to 2 percent of a normally solid thermoplastic alkenyl aromatic resin B selected from the group consisting of a polymerized monoalkenyl aromatic hydrocarbon of the benzene series having a single ethylenically unsaturated group of the formula ACH2=CR wherein R represents a member of the group consisting of hydrogen, methyl and ethyl radicals, said group being directly attached to a carbon atom of the benzene nucleus, which resin B contains not more than 3 percent by weight of volatile ingredients capable of being vaporized and removed by heating the resinat a temperature of 213 C. at one millimeter absolute pressure for a time of 25 minutes, is compatible with resin A and has an average molecular weight of not more than one-third as great as the average molecular weight of resin A and has a second order transition temperature at least as high as 45 C. and not more than 5 C. above the second order transition temperature of resin A.

2. A resinous composition according to claim l, wherein the thermoplastic alkenyl aromatic resins of A and B each contain not more than 2 percent by weight of said volatile ingredients.

3,. A resinojrs composition according to claim 1, where 17 in the thermoplastic alkenyl aromatic resins of A and B are employed in proportions corresponding to from 80 to 95 percent by Weight of said resin A and from 20 to 5 percent of said resin B.

4. A resinous composition according to claim 3, wherein the thermoplastic alkenyl aromatic resin of A is a copolymer of at least 60 percent by weight of styrene and not more than 40 percent of alpha-methyl styrene.

5. A resnous composition according to claim 3, wherein the thermoplastic alkenyl aromatic resin of A is polystyrene and the alkenyl aromatic resin of B is polymerized alpha-methyl styrene having an average molecular weight between 1,000 and 6,000.

6. A resinous composition according to claim 3, where- '18 in the thermoplastic alkcnyl aromatic resin of A is polystyrene and the resin of B is polystyrene having an average molecular weight between 10,000 and 60,000.

References Cited in the file of this patent UNITED STATES PATENTS OTHER REFERENCES Jenckel et al.: Zeit. physikal. Chem.; volume 182A, 1938, pages 361, 368, 369.

UNITED STATES PATENT OFFICE CERTIFICATE 0F CORRECTION Patent No,. 2,864,802' Deeember lo7 1958 Reymond Mo Pro'e et El.

It is hereby certified that error appears in the printed specification of the above numbered patent requiring correction and that the said Letters Patent should read as corrected below.

Column ll, line 63;, in the' table'g under 'YI'emperatnr'e'\5 GEN, for "995" read. A45 nl,

Signed and sealed this 21st day of July 195% (SEAL) Attest:

Commissioner of Patents Attesting Ocer 

1. A RESINOUS COMPOSITION CONSISTING OF FROM 60 TO 98 PERCENT BY WEIGHT OF A NORMALLY SOLID THERMOPLASTIC ALKENYL AROMATIC RESIN A SELECTED FROM THE GROUP CONSISTING OF (1) A POLYMERIZED MONOVINYL AROMATIC HYDROCARBON OF THE BENZENE SERIES, (2) COPOLYMERS OF AT LEAST 60 PERCENT BY WEIGHT OF A MONOVINYL AROMATIC HYDROCARBON OF THE BENZENE SERIES AND NOT MORE THAN 40 PERCENT OF AN ALKENYL AROMATIC HYDROCARBON OF THE BENZENE SERIES HAVING A SINGLE ISOPROPENYL RADICAL DIRECTLY ATTACHED TO A CARBON ATOM OF THE AROMATIC NUCLEUS AND (3) RESINOUS PRODUCTS CONSISTING OF FROM 60 TO 98 PERCENT BY WEIGHT OF AT LEAST ONE OF THE POLYMERS OF 1 AND 2 AND FROM 40 TO 2 PERCENT OF A RUBBERY ELASTOMER WHICH IS A MEMBER OF THE GROUP CONSISTING OF NATURAL RUBBER AND RUBBERY COPOLYMERS OF FROM 40 TO 80 PERCENT BY WEIGHT OF BUTADIENE AND FROM 60 TO 20 PERCENT OF STYRENE, THE SAID RESIN A CONTAINING NOT MORE THAN 3 PERCENT BY WEIGHT OF VOLATILE INGREDIENTS CAPABLE OF BEING VAPORIZED AND REMOVED BY HEATING THE RESIN AT A TEMPERATURE OF 213*C. AT ONE MILLIMETER ABSOLUTE PRESSURE FOR A TIME OF 25 MINUTES AND HAVING AN AVERAGE MOLECULAR WEIGHT OF AT LEAST 140,000, AS DETERMINED BY THE SCATTERING OF LIGHT, INTIMATELY INCORPORATED WITH 40 TO 2 PERCENT OF A NORMALLY SOLID THERMOPLASTIC ALKENYL AROMATIC RESIN B SELECTED FROM THE GROUP CONSISTING OF A POLYMERIZED MONOALKENYL AROMATIC HYDROCARBON OF THE BENZENE SERIES HAVING A SINGLE ETHYLENICALLY UNSATURATED GROUP OF THE FORMULA CH2=CR- WHEREIN R REPRESENTS A MEMBER OF THE GROUP CONSISTING OF HYDROGEN, METHYL AND ETHYL RADICALS, SAID GROUP BEING DIRECTLY ATTACHED TO A CARBON ATOM OF THE BENZENE NUCLEUS, WHICH RESIN B CONTAINS NOT MORE THAN 3 PERCENT BY WEIGHT OF VOLATILE INGREDIENTS CAPABLE OF BEING VAPORIZED AND REMOVED BY HEATING THE RESIN AT A TEMPERATURE OF 213*C. AT ONE MILLIMETER ABSOLUTE PRESSURE FOR A TIME OF 25 MINUTES, IS COMPATIBLE WITH RESIN A AND HAS AN AVERAGE MOLECULAR WEIGHT OF NOT MORE THAN ONE-THIRD AS GREAT AS THE AVERAGE MOLECULAR WEIGHT OF RESIN A AND HAS A SECOND ORDER TRANSITION TEMPERATURE AT LEAST AS HIGH AS 45*C. AND NOT MORE THAN 5*C. ABOVE THE SECOND ORDER TRANSITION TEMPERATURE OF RESIN A. 